JP2000087195A - High strength iron-base sintered alloy and its production - Google Patents
High strength iron-base sintered alloy and its productionInfo
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- JP2000087195A JP2000087195A JP10320626A JP32062698A JP2000087195A JP 2000087195 A JP2000087195 A JP 2000087195A JP 10320626 A JP10320626 A JP 10320626A JP 32062698 A JP32062698 A JP 32062698A JP 2000087195 A JP2000087195 A JP 2000087195A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、エンジン部品を
始めとする自動車部品およびコンプレッサー部品などの
各種機械部品の材料として使用される高密度で強度の優
れた鉄基焼結合金およびその製造方法に関するものであ
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-density, high-strength iron-based sintered alloy used as a material for various machine parts such as engine parts, automobile parts and compressor parts, and a method for producing the same. Things.
【０００２】[0002]
【従来の技術】一般に、エンジン部品を始めとする自動
車部品およびコンプレッサー部品などの各種機械部品の
材料として鉄基焼結合金が用いられており、この鉄基焼
結合金の１つとして、Ｃｕ：０．５〜９．７重量％、Ｎ
ｉ：０．００５〜３重量％、Ｃ：１．５重量％以下を含
有し、残りがＦｅおよび不可避不純物からなる組成を有
する鉄基焼結合金があることは知られている（特開昭６
１−１０４０５２号公報参照）。2. Description of the Related Art Generally, iron-based sintered alloys are used as materials for various mechanical parts such as engine parts, automobile parts and compressor parts. One of the iron-based sintered alloys is Cu: 0.5 to 9.7% by weight, N
It is known that there is an iron-based sintered alloy containing i: 0.005 to 3% by weight and C: 1.5% by weight or less, with the balance being Fe and unavoidable impurities (Japanese Patent Laid-Open No. 6
1-110452).
【０００３】[0003]
【発明が解決しようとする課題】しかし、近年、エンジ
ン部品を始めとする自動車部品およびコンプレッサー部
品などの各種機械部品の材料としてさらに高強度の鉄基
焼結合金が求められているが、従来の鉄基焼結合金では
強度が十分でなく、一層高強度の鉄基焼結合金が求めら
れている。However, in recent years, iron-based sintered alloys having higher strength have been demanded as materials for various mechanical parts such as engine parts, automobile parts and compressor parts. Iron-based sintered alloys do not have sufficient strength, and iron-based sintered alloys with higher strength are required.
【０００４】[0004]
【課題を解決するための手段】そこで、本発明者らは、
上述のような観点から、自動車部品およびコンプレッサ
ー部品などの各種機械部品の材料として使用することの
できる一層高強度の鉄基焼結合金を得るべく研究を行っ
ていたところ、（ａ）Ｃｕ：１５〜４０重量％、Ｎｉ：
０．５〜１５重量％、Ｃ：０．０００５〜０．８５重量
％を含有し、残りがＦｅおよび不可避不純物からなる組
成を有する鉄基焼結合金は、従来の鉄基焼結合金よりも
強度が格段に優れている、（ｂ）この（ａ）に記載の鉄
基焼結合金は、Ｆｅを主成分とするＦｅ基合金相をＣｕ
を主成分とするＣｕ基合金相で包囲することにより、Ｆ
ｅ基合金相とＦｅ基合金相をＣｕ基合金相により結合し
た状態の組織を有する、（ｃ）前記Ｆｅを主成分とする
Ｆｅ基合金相はＮｉ、ＣｕおよびＣを含みかつＦｅを５
０重量％以上含むＦｅ合金相であり、前記Ｃｕを主成分
とするＣｕ基合金相はＮｉ、ＦｅおよびＣを含みかつＣ
ｕを５０重量％以上含むＣｕ合金相であり、前記Ｆｅ基
合金相に含まれるＮｉおよびＣの濃度は、前記Ｃｕ基合
金相に含まれるＮｉおよびＣの濃度よりも大きいことが
一層好ましい、（ｄ）前記鉄基焼結合金の密度は、７．
０〜８．２Ｍｇ／ｍ3 の範囲内にあることが一層好まし
い、などの知見を得たのである。Means for Solving the Problems Accordingly, the present inventors have:
From the above viewpoints, research was conducted to obtain a higher-strength iron-based sintered alloy that can be used as a material for various mechanical parts such as automobile parts and compressor parts, and (a) Cu: 15 -40% by weight, Ni:
An iron-based sintered alloy containing 0.5 to 15% by weight and C: 0.0005 to 0.85% by weight, and having a balance of Fe and unavoidable impurities, is lower than a conventional iron-based sintered alloy. (B) The iron-based sintered alloy according to (a) has an Fe-based alloy phase containing Fe as a main component.
Is surrounded by a Cu-based alloy phase mainly composed of
(c) the Fe-based alloy phase containing Fe as a main component contains Ni, Cu, and C, and contains 5% Fe.
0% by weight or more, and the Cu-based alloy phase containing Cu as a main component contains Ni, Fe and C, and
It is a Cu alloy phase containing 50% by weight or more of u, and the concentration of Ni and C contained in the Fe-based alloy phase is more preferably higher than the concentrations of Ni and C contained in the Cu-based alloy phase. d) The density of the iron-based sintered alloy is 7.
It has been found that the content is more preferably in the range of 0 to 8.2 Mg / m 3 .
【０００５】この発明は、かかる知見にもとづいて成さ
れたものであって、（１）Ｃｕ：１５〜４０重量％、Ｎ
ｉ：０．５〜１５重量％、Ｃ：０．０００５〜０．８５
重量％を含有し、残りがＦｅおよび不可避不純物からな
る組成を有する高強度鉄基焼結合金、（２）Ｃｕ：１５
〜４０重量％、Ｎｉ：０．５〜１５重量％、Ｃ：０．０
００５〜０．８５重量％を含有し、残りがＦｅおよび不
可避不純物からなる組成を有し、かつＦｅを主成分とす
るＦｅ基合金相をＣｕを主成分とするＣｕ基合金相で結
合してなる組織を有する高強度鉄基焼結合金、（３）前
記Ｆｅを主成分とするＦｅ基合金相はＮｉ、Ｃｕおよび
Ｃを含みＦｅを５０重量％以上含むＦｅ合金相であり、
Ｃｕを主成分とするＣｕ基合金相はＮｉ、ＦｅおよびＣ
を含みＣｕを５０重量％以上含むＣｕ合金相であり、か
つＦｅ基合金相に含まれるＮｉおよびＣの濃度は、Ｃｕ
基合金相に含まれるＮｉおよびＣの濃度よりも大きい前
記（２）記載の高強度鉄基焼結合金、（４）前記高強度
鉄基焼結合金は、密度：７．０〜８．２Ｍｇ／ｍ3 を有
する前記（１）、（２）または（３）記載の高強度鉄基
焼結合金、に特徴を有するものである。The present invention has been made on the basis of the above findings. (1) Cu: 15 to 40% by weight, N
i: 0.5 to 15% by weight, C: 0.0005 to 0.85
Wt.%, The balance being Fe and unavoidable impurities, a high-strength iron-based sintered alloy, (2) Cu: 15
-40% by weight, Ni: 0.5-15% by weight, C: 0.0
005-0.85% by weight, the balance being composed of Fe and inevitable impurities, and combining an Fe-based alloy phase mainly composed of Fe with a Cu-based alloy phase mainly composed of Cu. A high-strength iron-based sintered alloy having the following structure: (3) The Fe-based alloy phase containing Fe as a main component is a Fe alloy phase containing Ni, Cu, and C and containing 50% by weight or more of Fe,
Cu-based alloy phase mainly composed of Cu is composed of Ni, Fe and C
Is a Cu alloy phase containing 50% by weight or more of Cu, and the concentration of Ni and C contained in the Fe-based alloy phase is Cu
The high-strength iron-based sintered alloy according to the above (2), which is higher than the concentrations of Ni and C contained in the base alloy phase, and (4) the high-strength iron-based sintered alloy has a density of 7.0 to 8.2 Mg. / M 3 , wherein the high-strength iron-based sintered alloy according to the above (1), (2) or (3) is characterized.
【０００６】この発明の高強度鉄基焼結合金は、Ｆｅ粉
末にＣｕ粉末およびＮｉ粉末の要素粉末を配合し、さら
に必要に応じてこれにＣ粉末を配合し混合して得られた
混合粉末を圧密成形し焼結して作ることができる。この
発明の高強度鉄基焼結合金のＣ含有量が極めて少ない場
合は、Ｃ粉末を添加することなくＦｅ粉末に含まれるＣ
を利用して製造することができる。この場合、Ｃｕ粉末
およびＮｉ粉末をＣｕ：１５〜４０重量％、Ｎｉ：０．
５〜１５重量％含むように配合する。[0006] The high-strength iron-based sintered alloy of the present invention is a mixed powder obtained by mixing element powders of Cu powder and Ni powder with Fe powder, and further mixing and mixing C powder as needed. Can be made by compacting and sintering. When the C content of the high-strength iron-based sintered alloy of the present invention is extremely small, the C content contained in the Fe powder without adding the C powder is increased.
It can be manufactured using. In this case, the Cu powder and the Ni powder are made of Cu: 15 to 40% by weight, Ni: 0.
It is blended so as to contain 5 to 15% by weight.
【０００７】したがって、この発明は、（５）Ｆｅ粉
末、Ｃｕ粉末およびＮｉ粉末を配合し混合して混合粉末
を作製し、この混合粉末を圧密成形し焼結する高強度鉄
基焼結合金の製造方法、（６）Ｆｅ粉末、Ｃｕ粉末、Ｎ
ｉ粉末および黒鉛が析出しない量のＣ粉末を配合し混合
して混合粉末を作製し、この混合粉末を圧密成形し焼結
する高強度鉄基焼結合金の製造方法、（７）前記Ｃｕ粉
末およびＮｉ粉末は、Ｃｕ：１５〜４０重量％、Ｎｉ：
０．５〜１５重量％含むように配合する（５）または
（６）記載の高強度鉄基焼結合金の製造方法、に特徴を
するものである。Accordingly, the present invention provides (5) a high-strength iron-based sintered alloy in which Fe powder, Cu powder and Ni powder are blended and mixed to produce a mixed powder, and the mixed powder is compacted and sintered. Manufacturing method, (6) Fe powder, Cu powder, N
(i) a method for producing a high-strength iron-based sintered alloy in which a mixed powder is prepared by mixing and mixing i-powder and an amount of C powder that does not precipitate graphite, and consolidating and sintering the mixed powder; And Ni powder, Cu: 15 to 40% by weight, Ni:
The method according to (5) or (6), wherein the high-strength iron-based sintered alloy is blended so as to contain 0.5 to 15% by weight.
【０００８】この発明の高強度鉄基焼結合金は、前記
（５）、（６）および（７）記載の高強度鉄基焼結合金
の製造方法において、Ｃｕ粉末およびＮｉ粉末の要素粉
末に代えて、Ｃｕ−Ｎｉ合金粉末（Ｎｉ：２〜５０重量
％を含有し、残部がＣｕおよび不可避不純物からなる母
合金粉末）の形で配合することが一層好ましい。この場
合も鉄基焼結合金のＣ含有量が極めて少ない場合は、Ｃ
粉末を添加することなくＦｅ粉末に含まれるＣを利用し
て製造することができるし、Ｃｕ−Ｎｉ合金粉末をＣ
ｕ：１５〜４０重量％、Ｎｉ：０．５〜１５重量％含む
ように配合する。[0008] The high-strength iron-based sintered alloy according to the present invention is characterized in that in the method for producing a high-strength iron-based sintered alloy described in (5), (6) or (7) above, the element powder of Cu powder and Ni powder is used. Instead, it is more preferable to mix in the form of a Cu—Ni alloy powder (a mother alloy powder containing 2 to 50% by weight of Ni and the balance of Cu and unavoidable impurities). Also in this case, when the C content of the iron-based sintered alloy is extremely small,
It can be manufactured using C contained in Fe powder without adding powder, and Cu-Ni alloy powder
u: 15 to 40% by weight and Ni: 0.5 to 15% by weight.
【０００９】したがって、この発明は、（８）Ｆｅ粉末
にＣｕ−Ｎｉ合金粉末を配合し混合して混合粉末を作製
し、この混合粉末を圧密成形し焼結する高強度鉄基焼結
合金の製造方法、（９）Ｆｅ粉末、Ｃｕ−Ｎｉ合金粉末
および黒鉛が析出しない量のＣ粉末を配合し混合して混
合粉末を作製し、この混合粉末を圧密成形し焼結する高
強度鉄基焼結合金の製造方法、（10）前記Ｃｕ−Ｎｉ合
金粉末を、Ｃｕ：１５〜４０重量％、Ｎｉ：０．５〜１
５重量％含むように配合する（８）または（９）記載の
高強度鉄基焼結合金の製造方法、に特徴を有するもので
ある。Accordingly, the present invention provides (8) a high-strength iron-based sintered alloy in which a mixed powder is prepared by mixing and mixing a Cu-Ni alloy powder with an Fe powder, and then compacting and sintering the mixed powder. Manufacturing method, (9) High-strength iron-based sintering in which Fe powder, Cu-Ni alloy powder and C powder in an amount that does not precipitate graphite are mixed and mixed to produce a mixed powder, and the mixed powder is compacted and sintered. (10) The Cu—Ni alloy powder is prepared by adding 15 to 40% by weight of Cu and 0.5 to 1% of Ni.
The method according to (8) or (9), wherein the high-strength iron-based sintered alloy is blended so as to contain 5% by weight.
【００１０】この発明の高強度鉄基焼結合金の製造方法
をさらに具体的に述べると、原料粉末として、Ｆｅ粉
末、Ｃ粉末、Ｃｕ粉末、Ｎｉ粉末およびＣｕ−Ｎｉ合金
粉末を用意し、Ｆｅ粉末にＣｕ：１５〜４０重量％、Ｎ
ｉ：０．５〜１５重量％含むようにＣｕ−Ｎｉ合金粉
末、またはＣｕ粉末およびＮｉ粉末を配合し、さらに得
られた配合粉末に金型成形時の潤滑剤（例えば、ステア
リン酸亜鉛粉末またはエチレンビスステアラミド）を添
加してダブルコーンミキサーで混合し、プレス成形して
圧粉体を作製し、圧粉体を水素を含む窒素雰囲気中、温
度：１１００〜１３００℃（一層好ましくは１１１０〜
１２５０℃）で焼結する。The method for producing a high-strength iron-based sintered alloy according to the present invention will be described in more detail. Fe powder, C powder, Cu powder, Ni powder, and Cu-Ni alloy powder are prepared as raw material powders. Cu in powder: 15-40% by weight, N
i: Cu-Ni alloy powder or Cu powder and Ni powder are blended so as to contain 0.5 to 15% by weight, and the obtained blended powder is lubricated at the time of molding (for example, zinc stearate powder or Ethylenebisstearamide) is added, mixed with a double cone mixer, and press-molded to produce a green compact. The green compact is placed in a nitrogen atmosphere containing hydrogen at a temperature of 1100 to 1300 ° C (more preferably 1110 to 1300 ° C).
(1250 ° C).
【００１１】この発明の高強度鉄基焼結合金の製造方法
において、Ｃｕ粉末およびＮｉ粉末の要素粉末よりもＣ
ｕ−Ｎｉ合金粉末を配合する方が好ましい理由は、Ｃｕ
−Ｎｉ合金粉末を配合して得られた混合粉末の焼結が下
記のメカニズムによるものと考えられる。すなわち、Ｃ
ｕ−Ｎｉ合金粉末を配合すると、焼結初期段階において
Ｃｕ−Ｎｉ合金の固液共存域に昇温されても一気に大量
のＣｕ液相が発生するのではなく、穏やかに焼結が進行
し、焼結体に歪み、撓みなどの変形は生じさせない。焼
結中期段階において、Ｃｕ−Ｎｉ合金粉末のＮｉはＦｅ
との親和性が高いため、Ｆｅ粉末中に拡散する。Ｆｅ粉
末中のＮｉ濃度が高くなるとＣｕのＦｅへの固溶限が高
くなるため、ＦｅへのＣｕの拡散も活発になり、Ｆｅと
Ｃｕの密着性が向上する。焼結後期段階においては、Ｃ
ｕ−Ｎｉ合金相中のＮｉ含有量が低下しているため、Ｃ
ｕ−Ｎｉ合金粉末の融点が下がり、一気に多量の液相が
発生し、ダイナミックな液相焼結が進行する。なお、焼
結後期段階において一気に多量の液相が発生しても、既
に十分な焼結が進行した後であるので焼結体に歪み、撓
みは発生しない。[0011] In the method for producing a high-strength iron-based sintered alloy according to the present invention, the elemental powder of Cu powder and Ni powder has a higher C content.
The reason why it is preferable to mix the u-Ni alloy powder is that Cu
It is considered that sintering of the mixed powder obtained by blending the -Ni alloy powder is due to the following mechanism. That is, C
When the u-Ni alloy powder is blended, a large amount of Cu liquid phase is not generated at a stretch even if the temperature is raised to the solid-liquid coexistence region of the Cu-Ni alloy in the initial stage of sintering, and sintering proceeds gently, Deformation such as distortion and bending does not occur in the sintered body. In the middle stage of sintering, Ni of the Cu-Ni alloy powder is Fe
It has high affinity for and diffuses into Fe powder. When the Ni concentration in the Fe powder is increased, the solid solubility limit of Cu in Fe is increased, so that the diffusion of Cu into Fe is activated and the adhesion between Fe and Cu is improved. In the later stage of sintering, C
Since the Ni content in the u-Ni alloy phase is low, C
The melting point of the u-Ni alloy powder is lowered, a large amount of liquid phase is generated at a stretch, and dynamic liquid phase sintering proceeds. Note that even if a large amount of liquid phase is generated at a stretch in the latter stage of sintering, the sintered body is not distorted or bent since sufficient sintering has already progressed.
【００１２】つぎに、この発明の高強度鉄基焼結合金の
成分組成を上記のごとく限定した理由について説明す
る。 （ａ）Ｃｕ Ｃｕは、密度、強度および耐摩耗性を向上させる効果が
あるが、その含有量が１５重量％未満ではその効果が十
分でなく、一方、４０重量％を越えるとかえって強度が
低下するようになるので好ましくない。したがって、Ｃ
ｕの含有量は１５〜４０重量％に定めた。Ｃｕの含有量
の一層好ましい範囲は１７〜３５重量％であり、さらに
一層好ましい範囲は１９〜３０重量％である。Next, the reason why the component composition of the high-strength iron-based sintered alloy of the present invention is limited as described above will be described. (A) Cu Cu has the effect of improving the density, strength and abrasion resistance. However, if its content is less than 15% by weight, its effect is not sufficient, while if it exceeds 40% by weight, the strength is rather reduced. Is not preferred. Therefore, C
The content of u is set to 15 to 40% by weight. A more preferred range for the Cu content is 17-35% by weight, and an even more preferred range is 19-30% by weight.
【００１３】（ｂ）Ｎｉ Ｎｉは、Ｃｕ合金相中においてＣｕ合金相の融点を上昇
させ、液相焼結をコントロールし、また強度および靭性
を向上させる作用があるが、その含有量が０．５重量％
未満ではその効果が十分でなく、一方、１５重量％を越
えて含有してもそれ以上の効果が少ない。したがって、
Ｎｉの含有量は０．５〜１５重量％に定めた。Ｎｉの含
有量の一層好ましい範囲は１〜４重量％である。(B) Ni Ni has the effect of increasing the melting point of the Cu alloy phase in the Cu alloy phase, controlling liquid phase sintering, and improving strength and toughness. 5% by weight
If the content is less than 15% by weight, the effect is not sufficient. Therefore,
The content of Ni was set to 0.5 to 15% by weight. A more preferable range of the Ni content is 1 to 4% by weight.
【００１４】（ｃ）Ｃ Ｃは、Ｆｅ粉末およびＣｕ−Ｎｉ合金粉末を還元しまた
強度および硬さを向上させる作用があるが、その含有量
が０．０００５重量％未満では効果が十分でなく、一
方、０．８５重量％を越えて含有するとＣｕ合金液相の
Ｆｅ粉末粒界への浸透を阻害して空孔を発生させ、さら
にＦｅ粉末が微細化を阻害するとともに黒鉛粒子が素地
中に析出して強度および靭性を低下させるので好ましく
ない。したがって、Ｃの含有量は０．０００５〜０．８
５重量％に定めた。Ｃの含有量の一層好ましい範囲は
０．００１〜０．３重量％であり、さらに一層好ましい
範囲は０．００２〜０．２重量％である。(C) C C has the effect of reducing Fe powder and Cu—Ni alloy powder and improving strength and hardness, but if its content is less than 0.0005% by weight, the effect is not sufficient. On the other hand, if the content exceeds 0.85% by weight, the penetration of the Cu alloy liquid phase into the grain boundaries of the Fe powder is hindered, and vacancies are generated. Undesirably, so that the strength and toughness are reduced. Therefore, the content of C is 0.0005 to 0.8.
It was determined to be 5% by weight. A more preferable range of the content of C is 0.001 to 0.3% by weight, and an even more preferable range is 0.002 to 0.2% by weight.
【００１５】[0015]
【発明の実施の形態】原料粉末として、平均粒径：５５
μｍのＦｅ粉末、表１に示される平均粒径および成分組
成を有するＣｕ−Ｎｉ合金粉末Ａ〜Ｅ、平均粒径：１０
μｍのＣｕ粉末、平均粒径：５μｍのＮｉ粉末および平
均粒径：１８μｍの黒鉛粉末を用意した。BEST MODE FOR CARRYING OUT THE INVENTION The raw material powder has an average particle size of 55.
μm Fe powder, Cu—Ni alloy powders A to E having the average particle size and component composition shown in Table 1, average particle size: 10
A Cu powder of μm, a Ni powder having an average particle diameter of 5 μm, and a graphite powder having an average particle diameter of 18 μm were prepared.
【００１６】[0016]
【表１】 [Table 1]
【００１７】実施例１ 前記Ｆｅ粉末、表１に示されるＣｕ−Ｎｉ合金粉末Ａ〜
Ｅ、および黒鉛粉末を表２〜表３に示される配合組成と
なるように配合し、さらに金型成形時の潤滑剤であるス
テアリン酸亜鉛粉末を外掛けで０．８重量％に当たる量
だけ添加してダブルコーンミキサーで混合し、プレス成
形して３０ｍｍ×１２ｍｍ×６ｍｍの寸法を有する圧粉
体を作製した。この圧粉体をＮ2 −５％Ｈ2 の混合雰囲
気中、温度：１１２０℃、２０分保持の条件で焼結した
のち、０．５℃／ｓｅｃの冷却速度で冷却し、表２〜表
３に示される成分組成を有する本発明焼結合金１〜１
４、比較焼結合金１〜５および従来焼結合金を作製し
た。Example 1 The Fe powder, Cu-Ni alloy powders A to A shown in Table 1
E, and graphite powder were blended so as to have the composition shown in Tables 2 and 3, and zinc stearate powder, which is a lubricant at the time of molding, was added in an amount equivalent to 0.8% by weight on the outside. Then, the mixture was mixed by a double cone mixer and press-molded to produce a green compact having a size of 30 mm × 12 mm × 6 mm. This green compact was sintered in a mixed atmosphere of N 2 -5% H 2 at a temperature of 1120 ° C. for 20 minutes and then cooled at a cooling rate of 0.5 ° C./sec. Inventive sintered alloys 1 to 1 having the component compositions shown in No. 3
4. Comparative sintered alloys 1 to 5 and conventional sintered alloys were produced.
【００１８】得られた本発明焼結合金１〜１４、比較焼
結合金１〜５および従来焼結合金の密度を測定し、その
結果を表４〜表５に示したのち、さらにこれら焼結合金
をＩＳＯ３３２５に基づき、支点間距離２５ｍｍで抗折
試験を行うことにより抗折力を測定し、またロックウェ
ルＢスケール硬さを測定し、その結果を表４〜表５に示
した。The densities of the obtained sintered alloys 1 to 14, comparative sintered alloys 1 to 5 and conventional sintered alloys were measured, and the results are shown in Tables 4 to 5. Gold was subjected to a bending test at a distance between fulcrums of 25 mm based on ISO 3325 to measure the bending strength, and the Rockwell B scale hardness was measured. The results are shown in Tables 4 and 5.
【００１９】さらに、前記ダブルコーンミキサーで混合
して得られた混合粉末をプレス成形して圧粉体を作製
し、この圧粉体をＮ2 −５％Ｈ2 の混合雰囲気中、温
度：１１２０℃、２０分保持の条件で焼結したのち、
０．５℃／ｓｅｃの冷却速度で冷却し、表２〜表３に示
される成分組成を有する本発明焼結合金１〜１４、比較
焼結合金１〜５および従来焼結合金からなるＪＩＳＺ２
２４２に準じたノッチ無しのシャルピー衝撃試験片を作
製した。これらシャルピー衝撃試験片を用いてシャルピ
ー衝撃値を測定し、その結果を表４〜表５に示した。Further, the mixed powder obtained by mixing with the double cone mixer is press-molded to produce a green compact, and the green compact is heated in a mixed atmosphere of N 2 -5% H 2 at a temperature of 1120. After sintering at ℃ for 20 minutes,
Cooled at a cooling rate of 0.5 ° C./sec, JISZ2 comprising the sintered alloys 1 to 14 of the present invention, comparative sintered alloys 1 to 5 and conventional sintered alloys having the component compositions shown in Tables 2 and 3
A notched Charpy impact test specimen according to H.242 was prepared. The Charpy impact value was measured using these Charpy impact test pieces, and the results are shown in Tables 4 and 5.
【００２０】さらに、前記本発明焼結合金１〜１４の微
細組織の成分含有量をＥＰＭＡにより測定した結果、前
記Ｆｅ基合金相はＮｉ、ＣｕおよびＣを含みかつＦｅを
５０重量％以上含み、前記Ｃｕ基合金相はＮｉ、Ｆｅお
よびＣを含みかつＣｕを５０重量％以上含み、さらにＦ
ｅ基合金相に含まれるＮｉおよびＣの濃度は、Ｃｕ基合
金相に含まれるＮｉおよびＣの濃度よりも大きいことを
確認した。Furthermore, as a result of measuring the component content of the microstructure of the sintered alloys 1 to 14 of the present invention by EPMA, the Fe-based alloy phase contains Ni, Cu and C, and contains 50% by weight or more of Fe, The Cu-based alloy phase contains Ni, Fe and C, and contains Cu in an amount of 50% by weight or more.
It was confirmed that the concentrations of Ni and C contained in the e-based alloy phase were higher than the concentrations of Ni and C contained in the Cu-based alloy phase.
【００２１】[0021]
【表２】 （本発明焼結合金１０のＣ量は原料粉末のＦｅ粉末に含まれるＣ量を調節するこ とにより調整した）[Table 2] (The C content of the sintered alloy 10 of the present invention was adjusted by adjusting the C content contained in the Fe powder of the raw material powder.)
【００２２】[0022]
【表３】 （＊印は、この発明の条件から外れた値を示す。）[Table 3] (The asterisk indicates a value outside the conditions of the present invention.)
【００２３】[0023]
【表４】 [Table 4]
【００２４】[0024]
【表５】 [Table 5]
【００２５】表２〜表５に示される結果から、本発明焼
結合金１〜１４と従来焼結合金を比較すると、本発明焼
結合金１〜１４は従来焼結合金と比べて、密度が高く、
抗折力、ロックウェルＢスケール硬さおよびシャルピー
衝撃値が高い値を示すことが分かる。しかし、この発明
の範囲から外れている成分組成を有する比較焼結合金１
〜５は、密度、抗折力、ロックウェル硬さおよびシャル
ピー撃値のうちの少なくともいずれかが劣ることが分か
る。From the results shown in Tables 2 to 5, when the sintered alloys 1 to 14 of the present invention are compared with the conventional sintered alloys, the sintered alloys 1 to 14 of the present invention have a higher density than the conventional sintered alloys. high,
It can be seen that the transverse rupture strength, Rockwell B scale hardness and Charpy impact value show high values. However, the comparative sintered alloy 1 having a component composition outside the scope of the present invention
It can be seen that the samples No. to No. 5 are inferior in at least one of density, bending strength, Rockwell hardness and Charpy impact value.
【００２６】実施例２ Ｆｅ粉末、Ｃｕ粉末、Ｎｉ粉末および黒鉛粉末を表６に
示される配合組成となるように配合し、さらに金型成形
時の潤滑剤であるステアリン酸亜鉛粉末を外掛けで０．
８重量％に当たる量だけ添加してダブルコーンミキサー
で混合し、プレス成形して３０ｍｍ×１２ｍｍ×６ｍｍ
の寸法を有する圧粉体を作製した。この圧粉体をＮ2 −
５％Ｈ2 の混合雰囲気中、温度：１１２０℃、２０分保
持の条件で焼結したのち、０．５℃／ｓｅｃの冷却速度
で冷却し、表６に示される成分組成を有する本発明焼結
合金１５〜２４を作製した。Example 2 Fe powder, Cu powder, Ni powder and graphite powder were blended so as to have the composition shown in Table 6, and zinc stearate powder as a lubricant at the time of molding was externally applied. 0.
8% by weight was added, mixed with a double cone mixer, press-molded and 30mm x 12mm x 6mm
A green compact having the following dimensions was produced. The green compact N 2 -
After sintering in a mixed atmosphere of 5% H 2 at a temperature of 1120 ° C. and holding for 20 minutes, it was cooled at a cooling rate of 0.5 ° C./sec, and sintered according to the present invention having the component composition shown in Table 6. Bonding golds 15 to 24 were produced.
【００２７】得られた本発明焼結合金１５〜２４の密度
を測定し、その結果を表７に示したのち、さらにこれら
焼結合金をＩＳＯ３３２５に基づき、支点間距離２５ｍ
ｍで抗折試験を行うことにより抗折力を測定し、またロ
ックウェルＢスケール硬さを測定し、その結果を表７に
示した。The densities of the obtained sintered alloys 15 to 24 of the present invention were measured, and the results are shown in Table 7. Further, these sintered alloys were further subjected to ISO 3325 based on the distance between fulcrums of 25 m.
The bending force was measured by conducting a bending test at m, and the Rockwell B scale hardness was measured. The results are shown in Table 7.
【００２８】さらに、前記ダブルコーンミキサーで混合
して得られた混合粉末をプレス成形して圧粉体を作製
し、この圧粉体をＮ2 −５％Ｈ2 の混合雰囲気中、温
度：１１２０℃、２０分保持の条件で焼結したのち、
０．５℃／ｓｅｃの冷却速度で冷却し、表６に示される
成分組成を有する本発明焼結合金１５〜２４からなるＪ
ＩＳＺ２２４２に準じたノッチ無しのシャルピー衝撃試
験片を作製した。これらシャルピー衝撃試験片を用いて
シャルピー衝撃値を測定し、その結果を表７に示した。Further, the mixed powder obtained by mixing with the double cone mixer is press-molded to produce a green compact, and the green compact is heated in a mixed atmosphere of N 2 -5% H 2 at a temperature of 1120. After sintering at ℃ for 20 minutes,
Cooled at a cooling rate of 0.5 ° C./sec, and made of the sintered alloys 15 to 24 of the present invention having the component compositions shown in Table 6.
A notched Charpy impact test specimen according to ISZ2242 was prepared. The Charpy impact value was measured using these Charpy impact test pieces, and the results are shown in Table 7.
【００２９】[0029]
【表６】 （本発明焼結合金２４のＣ量は原料粉末のＦｅ粉末に含まれるＣ量を調節するこ とにより調整した）[Table 6] (The C content of the sintered alloy 24 of the present invention was adjusted by adjusting the C content contained in the Fe powder of the raw material powder.)
【００３０】[0030]
【表７】 [Table 7]
【００３１】表６および表７に示される結果から、本発
明焼結合金１５〜２４はいずれも実施例１の表５に示さ
れる従来焼結合金と比べて、密度が高く、抗折力、ロッ
クウェルＢスケール硬さおよびシャルピー衝撃値が高い
値を示すことが分かる。さらに、前記本発明焼結合金１
５〜２４の微細組織の成分含有量をＥＰＭＡにより測定
した結果、前記Ｆｅ基合金相はＮｉ、ＣｕおよびＣを含
みかつＦｅを５０重量％以上含み、前記Ｃｕ基合金相は
Ｎｉ、ＦｅおよびＣを含みかつＣｕを５０重量％以上含
み、さらにＦｅ基合金相に含まれるＮｉおよびＣの濃度
は、Ｃｕ基合金相に含まれるＮｉおよびＣの濃度よりも
大きいことを確認した。From the results shown in Tables 6 and 7, all of the sintered alloys 15 to 24 of the present invention have a higher density, a higher transverse rupture strength, and a lower density than the conventional sintered alloys shown in Table 5 of Example 1. It can be seen that Rockwell B scale hardness and Charpy impact value show high values. Further, the sintered alloy of the present invention 1
As a result of measuring the component contents of 5 to 24 microstructures by EPMA, the Fe-based alloy phase contains Ni, Cu, and C, and 50% by weight or more of Fe, and the Cu-based alloy phase contains Ni, Fe, and C. And Cu in an amount of 50% by weight or more, and the concentrations of Ni and C contained in the Fe-based alloy phase were higher than the concentrations of Ni and C contained in the Cu-based alloy phase.
【００３２】[0032]
【発明の効果】上述のように、この発明の鉄基焼結合金
は、密度および抗折力が高い値を示し、さらにロックウ
ェルＢスケール硬さおよびシャルピー衝撃値が高い値を
示すことから、強度、靭性および硬さに優れ、自動車部
品およびコンプレッサー部品などの各種機械部品の材料
として適しており、機械産業の発展に大いに貢献し得る
ものである。As described above, the iron-based sintered alloy of the present invention exhibits high values of density and transverse rupture strength, and also exhibits high values of Rockwell B scale hardness and Charpy impact value. Excellent in strength, toughness and hardness, it is suitable as a material for various machine parts such as automobile parts and compressor parts, and can greatly contribute to the development of the machine industry.
Claims (10)
〜１５重量％、Ｃ：０．０００５〜０．８５重量％を含
有し、残りがＦｅおよび不可避不純物からなる組成を有
することを特徴とする高強度鉄基焼結合金。1. Cu: 15 to 40% by weight, Ni: 0.5
A high-strength iron-based sintered alloy containing 〜15% by weight and C: 0.0005-0.85% by weight, with the balance being Fe and unavoidable impurities.
〜１５重量％、Ｃ：０．０００５〜０．８５重量％を含
有し、残りがＦｅおよび不可避不純物からなる組成を有
し、かつＦｅを主成分とするＦｅ基合金相をＣｕを主成
分とするＣｕ基合金相で結合してなる組織を有すること
を特徴とする高強度鉄基焼結合金。2. Cu: 15 to 40% by weight, Ni: 0.5
-15% by weight, C: 0.0005-0.85% by weight, the balance being a composition comprising Fe and unavoidable impurities, and a Fe-based alloy phase containing Fe as a main component containing Cu as a main component. A high-strength iron-based sintered alloy characterized by having a structure formed by bonding with a Cu-based alloy phase.
Ｎｉ、ＣｕおよびＣを含みＦｅを５０重量％以上含むＦ
ｅ合金相であり、Ｃｕを主成分とするＣｕ基合金相はＮ
ｉ、ＦｅおよびＣを含みＣｕを５０重量％以上含むＣｕ
合金相であり、かつＦｅ基合金相に含まれるＮｉおよび
Ｃの濃度は、Ｃｕ基合金相に含まれるＮｉおよびＣの濃
度よりも大きいことを特徴とする請求項２記載の高強度
鉄基焼結合金。3. The Fe-based alloy phase containing Fe as a main component contains Ni, Cu and C, and contains F at 50% by weight or more.
e alloy phase, and the Cu-based alloy phase containing Cu as a main component is N
Cu containing i, Fe and C and containing at least 50% by weight of Cu
The high-strength iron-based sintering according to claim 2, wherein the concentration of Ni and C contained in the Fe-based alloy phase is higher than the concentrations of Ni and C contained in the Cu-based alloy phase. Binding gold.
０〜８．２Ｍｇ／ｍ 3 を有することを特徴とする請求項
１、２または３記載の高強度鉄基焼結合金。4. The high-strength iron-based sintered alloy has a density of: 7.
0 to 8.2 Mg / m ThreeClaims characterized by having
4. A high-strength iron-based sintered alloy according to 1, 2, or 3.
合し、圧密成形し、焼結することを特徴とする高強度鉄
基焼結合金の製造方法。5. A method for producing a high-strength iron-based sintered alloy, comprising mixing Fe powder, Cu powder and Ni powder, compacting and sintering.
鉛が析出しない量のＣ粉末を混合し、圧密成形し、焼結
することを特徴とする高強度鉄基焼結合金の製造方法。6. A method for producing a high-strength iron-based sintered alloy, comprising mixing Fe powder, Cu powder, Ni powder and C powder in such an amount that graphite is not precipitated, compacting and sintering.
５〜４０重量％、Ｎｉ：０．５〜１５重量％含むように
混合することを特徴とする請求項５または６記載の高強
度鉄基焼結合金の製造方法。7. The method according to claim 1, wherein the Cu powder and the Ni powder are Cu: 1
The method for producing a high-strength iron-based sintered alloy according to claim 5 or 6, wherein the mixing is carried out so as to contain 5 to 40% by weight and Ni: 0.5 to 15% by weight.
し、圧密成形し、焼結することを特徴とする高強度鉄基
焼結合金の製造方法。8. A method for producing a high-strength iron-based sintered alloy, comprising mixing a Fe—Powder powder with a Cu—Ni alloy powder, compacting, and sintering.
鉛が析出しない量のＣ粉末を混合し、圧密成形し、焼結
することを特徴とする高強度鉄基焼結合金の製造方法。9. A method for producing a high-strength iron-based sintered alloy, comprising mixing Fe powder, Cu-Ni alloy powder and C powder in such an amount that graphite is not precipitated, compacting and sintering.
５〜４０重量％、Ｎｉ：０．５〜１５重量％含むように
混合することを特徴とする請求項８または９記載の高強
度鉄基焼結合金の製造方法。10. The Cu—Ni alloy powder, Cu: 1
The method for producing a high-strength iron-based sintered alloy according to claim 8 or 9, wherein the mixing is carried out so as to contain 5 to 40% by weight and Ni: 0.5 to 15% by weight.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32062698A JP3346305B2 (en) | 1998-07-17 | 1998-11-11 | High strength iron-based sintered alloy |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20363898 | 1998-07-17 | ||
| JP10-203638 | 1998-07-17 | ||
| JP32062698A JP3346305B2 (en) | 1998-07-17 | 1998-11-11 | High strength iron-based sintered alloy |
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| Publication Number | Publication Date |
|---|---|
| JP2000087195A true JP2000087195A (en) | 2000-03-28 |
| JP3346305B2 JP3346305B2 (en) | 2002-11-18 |
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ID=26514039
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| Application Number | Title | Priority Date | Filing Date |
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5938354A (en) * | 1982-08-26 | 1984-03-02 | Toyota Motor Corp | Joined cam shaft made of sintered alloy |
| JPS60165307A (en) * | 1984-02-07 | 1985-08-28 | Nippon Piston Ring Co Ltd | Preparation of cam shaft |
| JPH0347944A (en) * | 1989-07-14 | 1991-02-28 | Sumitomo Metal Ind Ltd | Substrate material for heat radiation |
| JPH05271879A (en) * | 1992-01-31 | 1993-10-19 | Toshiba Corp | High strength spring member |
| JPH05306433A (en) * | 1992-03-05 | 1993-11-19 | Toshiba Corp | Wear resistant member |
| JPH0666117A (en) * | 1992-08-10 | 1994-03-08 | Toyota Motor Corp | Valve guide of internal combustion engine |
| JPH09143638A (en) * | 1995-11-20 | 1997-06-03 | Hitachi Powdered Metals Co Ltd | Ferrous sintered oil retaining bearing and its production |
| JPH09329007A (en) * | 1996-06-13 | 1997-12-22 | Nippon Piston Ring Co Ltd | Sinered alloy-made joint type valve seat and method for manufacturing joint type valve seat material |
-
1998
- 1998-11-11 JP JP32062698A patent/JP3346305B2/en not_active Expired - Fee Related
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5938354A (en) * | 1982-08-26 | 1984-03-02 | Toyota Motor Corp | Joined cam shaft made of sintered alloy |
| JPS60165307A (en) * | 1984-02-07 | 1985-08-28 | Nippon Piston Ring Co Ltd | Preparation of cam shaft |
| JPH0347944A (en) * | 1989-07-14 | 1991-02-28 | Sumitomo Metal Ind Ltd | Substrate material for heat radiation |
| JPH05271879A (en) * | 1992-01-31 | 1993-10-19 | Toshiba Corp | High strength spring member |
| JPH05306433A (en) * | 1992-03-05 | 1993-11-19 | Toshiba Corp | Wear resistant member |
| JPH0666117A (en) * | 1992-08-10 | 1994-03-08 | Toyota Motor Corp | Valve guide of internal combustion engine |
| JPH09143638A (en) * | 1995-11-20 | 1997-06-03 | Hitachi Powdered Metals Co Ltd | Ferrous sintered oil retaining bearing and its production |
| JPH09329007A (en) * | 1996-06-13 | 1997-12-22 | Nippon Piston Ring Co Ltd | Sinered alloy-made joint type valve seat and method for manufacturing joint type valve seat material |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3346305B2 (en) | 2002-11-18 |
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